Vol. 8, No. 5, September-October 1975
Scission of Polymer Chains by High-speed Stirring 677
Peterlin theory leads t o a n extra adjustable parameter, the actual physical meaning of which is poorly understood. Acknowledgment. This work was supported in p a r t by a g r a n t from the National Science Foundation. We are ind e b t e d t o Professors J. L. Schrag a n d R. B. Bird for valuable discussions, t o Professor M. K u r a t a for the polymer samples, and to Mr. F. H. M. Nestler and Miss Hsin H u a n g for help with calculations. J.W.M.N. is grateful to the Netherlands Organisation of the Advancement of P u r e Research (Z.W.O.) for receiving a travel grant.
References and Notes This investigation was part of the research program of the Rheology Research Center, University of Wisconsin. D. J. Massa, J. L. Schrag, and J. D. Ferry, Macromolecules, 4, 210 (1971). K. Osaki and J. L. Schrag, Polym. J . , 2, 541 (1971). J. W. M. Noordermeer, 0. Kramer, F. H. M. Nestler, J. L. Schrag, and J. D. Ferry, Macromolecules, 8,539 (1975). M. Iwama, H. Utiyama, and M. Kurata, J . Macromol. Chem., 1, 701 (1966). H. J. Cantow and G. V. Schultz,2. Phys. Chem. (Frankfurtam Main), 2, 117 (1954).
( 7 ) D. J. Massa and J . L. Schrag, J . Polym. Sei.,Part A - 2 , 10, 71 (19i21. (8) J. D. Ferry, “Viscoelastic Properties of Polymers”,2nd ed, Wiley, New York, N.Y., 1970. (9) P. E. Rouse, J. Chem. Phys., 21,1272 11953). (10) B. H. Zimm, J . Chem. Phys., 24,269 (1956). (11) A. S. Lodge and Y.-J. Wu, MRC Technical Summary Report No. 1260, Mathematics Research Center, University of Wisconsin, Madison, Wisconsin, 1972. (12) S. E. Lovell and J. D. F e r r y , J . Phys. Chem., 65,2274 (1961). (13) J. E. Frederick, N. W. Tschoegl, and J. D. Ferry, J . Phys. Chem., 68, 1974 (1964). F. C. Wang and B. H. Zimm, J . Poiym. Scl., Polym Phys E d , 12,1619, 1638 (1974). M. Fixman and J. Kovac,J. Chem Phys., 61.4939,4950 (1971). M. Kurata, private communication. G. B. Thurston and A. Peterlin,J . Chem. PhJs., 16,4881 (19671. A. Peterlin,J . Polym. Sci.,Purt A-2, 5 , 179 (1967). J. W. Miller and J. L. Schrag, Macromolecules, 8,361 (1975). E. Riande, H. Markovitz, D. J. Plazek, and N. Raghupathi, private communication. A. Peterlin and C. Reinhold, Trans. Soc Rheoi., 11,16 (1967). R. B. Bird, H. R. Warner, Jr., and D. C. Evans, Adc. Polym. Scr , 8, 1 (1971). 0. Hassager, J . Chem Phys., 60,2111,4001 (19741. H. Nakajima, M. Doi, K. Okano, and Y. Wada, Rep. Prog. Poiym.Phqs. J p n . , 16.91 (1973). M. Fixman and G. T. Evans, private communication.
Relationship between Hydrodynamic Volume and the Scission of Polymer Chains by High-speed Stirring in Several Solvents Akihiko Nakano and Y u j i M i n o u r a * Department of Polymer Chemistry, Research Institute for Atomic Energy, Osaka City University, Osaka, Japan. Received March 18,1975
ABSTRACT Five different vinyl polymers, poly(methy1 methacrylate), poly(methy1 acrylate), poly(a-methylstyrene), polystyrene, and polyisobutylene, were stirred at 30,000 rpm by a T. K. Homomixer a t a polymer concentration of 0.04% w/v in various solvents for 2 hr in order to investigate the relationship between final chain length and the hydrodynamic volume of the polymer chains in the solvents. After prolonged stirring a t low concentration the ruptured polymer chains reached a nearly constant hydrodynamic volume independent of the type of solvent, and polymers with higher Tg’s,Le., the more rigid polymers, attained lower hydrodynamic volumes. The results indicate that there is a relation between mechanical scission of polymer chains in solution and their hydrodynamic volume.
The authors have been studying various factors which affect the scission by high-speed ~ t i r r i n g l -of ~ solutions of long-chain polymers such as poly(methy1 methacrylate) a n d polystyrene. It has been found that the r a t e of scission of polymer chains is higher and the final chain length is shorter i n good t h a n in poor solvents at a low concentrat i ~ nBecause .~ polymer chains are more extended and thus have larger intrinsic viscosities in good than in poor solvents, the products of final chain lengths and their intrinsic viscosities in the results4 seemed to approach a constant value regardless of the kinds of solvents used at low concentrations. According to Flory,G the following equation holds for polymers in solution [q]M = +(6s2)3’2 where [q] is the intrinsic viscosity, M is the molecular is the meanweight, 9 is the Flory constant, a n d square distance of an element from the center of gravity. Therefore, t h e products described above c a n be estimated in terms of hydrodynamic volumes. In this study, t h e relationship between hydrodynamic volumes a n d the final chain lengths of various polymers was investigated after stirring at low concentration in several solvents.
(s2)
Experimental Section Materials. The linear long-chain polymers used for degradation were prepared as follows. Poly(methy1 methacrylate) (PMMA) was prepared in the same way as described in a previous paper.4 Viscosity average degree of polymerization, (p,), was 6250 and molecular weight, (M,), was 625,000. Polystyrenes (PSt-1 and PSt-2) with different molecular weights and molecular weight distributions were used. PSt-1 was described in the previous paper4 and PSt-2 was 2btained from Pressure Chemical Co. P, of PSt-1 was 5610-and M, was 583,000. The nominal molecular weight and M,/K,, of PSt-2 were 2,000,000 and less than 1.30, respectively. P , and M, of PSt-2 measured by the authors were 15,300 and 1,590,000,respectively. Poly(methy1 acrylate) (PMA) was spontaneously polymerized b y sunlight in a sealed glass container in the absence of initiator. P, was 17,800 and M, was 1,530,000. Poly(cymethylstyrene) (PaMSt) was obtained by polymerizing the purified monomer using living tetramer of a-methylstyrene obtained by rescting the monomer with sodium metal in THF. p , was 8980 and M, was 1,060,OOO. Polyisobutylene (PIB) (Visianex MML-100 sueplied by Esso Standard Petroleum Co.) had a P, of 16,500 and a M, of 927,000. Solvents were used after purifying by the usual methods. The P, and Mu values listed for the above polymers were determined from equations contained in the next section. Procedure. Solutions of each polymer (200 ml) in each solvent a t a given concentration were prepared and stirred at 30,000 f 500 rpm at 30 f 5 O for a given time by a high-speed mixer. The experiments with PSt-cyclohexane were carried out at 40 f 5 O . The
678 Nakano, Minoura
Macromolecules Table I Values of k and PIfor PMMA Solutions of Various Concentrations (30.000 rum. 30")
Ethyl acetate Benzene Chloroform I 0
40
20
Time,
60
80
J
100 120
2 0.2 0.04 2 0.2 0.04 2 0.2
13 14 21 14 22 10 20
0.04
40
30
,
3500 3170 2580 4440 3060 1920 4560 2110 1510
2630 2380 1940 3330 2300 1440 3420 1580 1130
2770 2490 1970 3400 2300 1470 3600 1650 1150
mln.
Figure 1. Falloff in molecular weight of PMMA in various solvents at 0.04% w/v during high-speed stirring (30,000rpm, 30°, 0.04% w/vh (0) ethyl acetate; ( 0 )benzene; ( 0 )chloroform. stirred polymer was recovered by evaporating the solvent and intrinsic viscosities were measured a t 30 f 0.02O in benzene, [ q ] ~ , and in each solvent used for stirring, However, the intrinsic viscosity of PSt-cyclohexane was measured at 40' with an Ubbelohde viscometer. Chain lengths of polymers &f, or P , were calculated from the following equations.
I n a good solvent
In a poor solvent
[VIS.
PMMA'
P,
PMA8
[q],
= 4.5 x 10-5fi,0
PaMStg
[TI,
= 24.9 X 10-5fiv0.647
PSt"
P , = 1770[q]B1,40
PIB"
[q], = 6.1 X 10-4fiv0.56
= 2200[9],'
Hyd rody namic Hydrodynamic volume volume
l3
78
It is more accurate to use the number average degree of polymerization, p,, to calculate the number of scissions described below, since the molecular weight distrib_ution_varieswith the scission of polymer chains. However, either P , or M, was used here for convenience. Gel permeation chromatographs for PMMA before stirring and after 2 hr of stirring gave nearly Gaussian distribut i o n ~which ,~ are not shown here. The above equations, therefore, were assumed t o be valid for polymers in this study. Stirring apparatus and procedure were described in detail in the previous paper.' A T. K. Homomixer of the M type made by Tokushu Kika Kogyo was used as a high-speed stirrer. Results a n d Discussion Scission of PMMA in Various Solvents by HighSpeed Stirring. The scission of PMMA chains in various solvents by high-speed stirring is shown below. The solutions containing PMMA in chloroform, benzene, and ethyl acetate a t 0.04% w/v were prepared and stirred for given times at 30,000 rpm a t 30'. Molecular weights of polymers recovered after stirring are shown in Figure 1. They decreased rapidly at first and then more slowly. The polymers were still degrading even after 2 hr of stirring. However, molecular weights obtained by stirring for 2 hr seem to approximate rather closely the final chain lengths for each solvent. Molecular weights of PMMA stirred at 0.04% w/v for 2 hr were highest for the poorest solvent, ethyl acetate; medium for the medium solvent, benzene; and lowest for the good solvent, chloroform. The M, vs. time curves can be converted to scission number vs. time plots by the method described in the previous paper' and expressed by Ovenall's equation dBJdt = k n , ( P , - PI),where k is the rate constant of scission and PI the limiting degree of polymerization below which polymers cannot be ruptured. Values of k and P I calculated by the method described in the previous paper' for experi-
Molecular weight
< Molecular
welght
Figure 2. Models of polymer in solvents after prolonged stirring. mental results on PMMA solution at various concentrations are shown in Table I. P , and P 2 h , in Table I represent the degrees of polymerization after infinite and 2-hr stirring, respectively. It is clear that P1 is higher at higher concentration in every solvent and that a t the lowest concentration, 0.04% w/v, P1 is higher in the poor solvent, and is lower in the good one. The latter observation seems to suggest that polymer chains degrade to a nearly constant hydrodynamic volume in those solvents. Because the interaction between polymer molecules is smaller and the rate of scission is higher at low concentrations, it seemed to be more appropriate to investigate the effect of solvent on the scission of polymer chain or to study the. relationship between the final chain length and the hydrodynamic volume a t lower Concentration. At the lowest concentration, the values of P 2 h r are very close to those of P , , indicating that they represent to a considereble extent the final values obtained from infinite stirring. Relationship between Final Chain Length a n d Hydrodynamic Volume. As seen above, P q h r , the degree of polymerization after 2 hr of stirring of a 0.04% solution was regarded as the value of final chain length. P l h r obtained for various polymers in several solvents are shown in Table I1 with other related values. The values of M 2 h r X [VIS were nearly constant regardless of the kind of solvent used for each polymer except the PaMSt-benzene, PSt-toluene, and PSt-benzene systems. m 2 h r X [VIS are values proportional to the hydrodynamic volumes. Therefore the calculated results mean that polymer chains were degraded to a nearly constant hydrodynamic volume in every solvent by high-speed stirring after relatively long time intervals as shown by models in Figure 2. Viewed from the standpoint of chain length, the values of P I were scattered but if they are ohserved from the
Scission of Polymer Chains by High-speed Stirring 679
Vol. 8, No. 5 , September-October 1975
Table I1 Degree of Polymerization, Intrinsic Viscosity, and Values Relating to Hydrodynamic Volume for Polymers Stirred for 2 h r in Various Solvents a t 0.04% w/v by High-speed Stirring (30,000 rpm, 30°Y
________
_____
-
________.I_-_ _ _ _ _ _ _ _ _ I -
%hJ[l$
Polymer
PSt
F,, =
15.300
T , = 100;
Solvent Chloroform Benzene Ethyl a c e t a t e Chloroform Benzene Ethyl a c e t a t e Benzene Dioxane C 1.1 1o r of o r m Benzene Toluene Dioxane Chloroform Ethyl a c e t a t e Methyl ethyl ketone (MEK) Benzene Toluene Dioxane Chloroform Ethyl a c e t a t e MEK Cyclohexaneb 1.2-Dichloroethane
P?hr
Lv,b.
db'g
FZhr[qL , dl/g
=
(6,?)''? 9. 10' dl/g
1150 1470 1970 2830 3970 3930 2020 1250 1390 1910 2080 1340 1060 2000 2230
0.873
1000
0.700 0.540 1.125 0.937 0.830 0.750 0.540 0.520 1.057 1.040 0.770 0.830 0.500 0.555
1030 1060 3180 3720 3260 1515 680 720 2020 2160 1030 880 1000 1240
1.00 1.03 1.a6 2.83 3.32 2.81 1.79 0.80 0.85 2.10 2.25 1.07 0.91 1.04 1.29
2330 2260 1460 1030 1810 1870 2210 1530
1.218 1.095 0.783 0.731 0.503 0.560 0.502 0.723
2840 2470 1140 7 53 910 1050 1110 1110
2.95 2.57 1.19 0.78 0.95 1.09 1.15 1.15
PIB I 16,500 T , = -73'
1260 0.7 1 0.720 1730 0.97 0.530 Po and P2 h l are the P, of polymers before stirring and after 2 hr of stirring at 0.04% w/v, respectively. [ q ] . is the [ q ] of the polymer in the solvent after stirring for 2 hr. * Data at 40". -Hexane Benzene
ii
standpoint of hydrodynamic volume, they converge to a nearly constant value or final hydrodynamic volume independent of the type of solvent. The results obtained for two types of PSt with different molecular weights and molecular weight distributions (MWD) are shown in Table 11. T h e values for the same solvent were not identical but were scattered. However, no meaningful difference was found between the two kinds of PSt. It was found that P S t chains were ruptured to a nearly constant hydrodynamic volume regardless of MWD of initial polymer and solvent. The Mark-Houwink-Sakurada equations used to obtain P , or M, are varied and Flory's constant, 9, can vary with the type of polymer. Therefore it would be a mistake to res being precisely proportional gard the values of M 2 h r [ ~ ]as to and to use them for comparisons between different polymers even if it is possible for a single polymer. Nevertheless, comparisons were made between polymer analogs. It is found that the values of & f 2 h r [ 7 ] ~ for PMMA and PaMSt are smaller than those for PMA and PSt and that the former polymers gave a smaller hydrodynamic volume than the latter. PMMA and P a M S t are considered to be derivatives of PMA and PSt whose hydrogen atom on a carbon is substituted with a methyl group and as a result the rotation of the main chains of the methyl substituted polymers are more restricted than those of PMA and PSt. Rigidities of PMMA and PaMSt are thought to be higher than those of PMA and PSt and, as shown in Table 11, the
(s2)3'2
1800 3270
glass transition temperature, T,, increases with chain stiffness. Consequently, the experimental results show that chain scission by a shearing force depends on the rigidity of a polymer chain and that a main chain with higher rigidity is more easily broken. There might be some relation between dimensions of the hydrodynamic volume and the rigidities of polymers. The values of f i 2 h r [ v ] S for PIB were rather small. Unfortunately, no corresponding derivative polymer, i.e., polypropylene, with a high enough M, for degradation could be obtained for comparison. The above data on &f2hr[v]S were widely scattered for PSt and PaMSt in benzene and toluene, showing that their molecular volumes after breaking were about twice as large as those of the other polymers. The reason for the scattering is unknown. It may be possible that the rate of degradation for these systems was too low for M * h r to represent the final chain length. Furthermore it might be caused by other factors relating to bond scission in the macromolecules. If experiments had been carried out a t lower concentrations, the data on !i?2hr[q]s may have shown less scattering. Mechanism of Scission. The results can be interpreted as follows. Polymer molecules were so well extended in good solvents that the larger molecules received a strong enough shear stress to break main chains into shorter segments. Under identical experimental conditions, molecules ruptured to below a certain limiting hydrodynamic volume no longer are subject to shear forces large enough to cause further chain scission.
680 Jones, Felderhof, Deutch
Macromolecules
If polymer chains are ruptured to a constant hydrodynamic volume, it is reasonable to assume that they are broken to a shorter average chain length in a good solvent. They may be highly extended12 when they receive a shear stress strong enough to break polymer bonds. According to Harrington and Zimm,12polymers are considerably extended under a large velocity gradient and under such conditions the Gaussian coil model is no longer possible. On the other hand, the rate constant of scission is considered to be highest near the center of polymer molec u l e ~ under ~ ~ - the ~ ~conditions described in this report, and it is assumed that the shearing forces become smaller away from the center. Such a heterogeneous distribution of shearing forces along polymer chains might affect the shape of the coils. The authors suppose that polymer molecules are deformed to something like the shape of the infinity symbol, “ m ” , under such shearing forces. Therefore the models shown in Figure 2 ought to be corrected to flat ellipses or stretched shapes under a high velocity gradient. In any event, the authors suspect from the results that, even under a large velocity gradient, the hydrodynamic volume has a certain relation to the scission of a polymer chain in solution by high-speed stirring.
Acknowledment. A part of the study was presented a t the 23rd Kobunshi Toronkai of the Society of Polymer Science in Japan, October, 1974. References a n d Notes Y . Minonra, T. Kasuya, S. Kawamura, and A. Nakano, J . Polym. Sci., Part A - 2 , 5, 125 (1967). A. Nakano and Y. Minoura, J . A p p l . Polym. Sci., 15,927 (1971). A . Nakano and Y. Minoura, J . A p p l . Polym. Sci., 16,627 (1972). A. Nakano and Y. Minoura, J . A p p l . Polym. Sci., in press.
A. Nakano and Y. Minoura, J . A p p l . Polym. Sci., in press. P. J. Flory and T. G. Fox, J . A m . Chem Soc., 73,1904 (1951). A. V. Tobolsky. J . Polym. Sci., 9,171 (1952). S. Krause, “Dilute Solution Properties of Acrylic and Methacrylic Polymers”. 1961. S.Okamura, T. Higashimura, and Y. Imanishi, Kobunshi Kagaku, 16, 244 (1951). A. V. Tobolsky, J . A m . Chem. Soc., 74,938 (1952). T. Fox, Jr., and P. J. Flory, J . Phys. Colloid Chem., 53, 197 (1949). R. E. Harrington and B. H . Zimm, J . Phys. Chem.,69,161 (1965). T. Fukutomi, M. Tsukada, T. Kakurai, and T. Noguchi, Polym. J., 3, 717 (19i2). P. A. R. Glynn, B. M. E. van der Hoff. and P. M. Reilly, J . Macromol. S c i . , Chem., 6, 1653 (1972). P. A. R. Glynn and B. M. E. van der Hoff, J . Macromol. Sci., Chem., 7, 1695 (1973).
Diffusion of Polymers Along a Fluid-Fluid Interface R. B. Jones,’* B. U. Felderhof,ln a n d J. M. Deutch*lb Department ofPhysics, Queen Mary College, London E l 4NS, England, and t h e Department of Chemistry, Massachusetts Institute of Technology, Cambridge, Massachusetts 02139. Received December 27,1974
ABSTRACT: We evaluate the diffusion coefficient for the motion of a polymer along the interface between two fluids. Two polymer models are considered: rigid rods oriented a t right angles to the interface, and spherical molecules with their center in the interface.
I. Introduction The influence of bounding surfaces on the motion of a solid body immersed in a fluid was first investigated by Lorentz2a in 1896. He studied the motion of a sphere near a plane wall using a perturbation method, the so-called method of reflections. Subsequently the effect of wall geometry on the motion of more complicated objects has been studied in great detail by the same method.2b In the present article we consider the effect of geometry on the motion of polymers, regarded as diffuse objects rather than as solid bodies. In particular we study the translational diffusion of a polymer adsorbed a t the interface between two immiscible fluids. Our primary motivation for studying this problem is the present interest in interfacial phenomena, particularly with regard to the adsorption and mobility of polymeric species at fluid surfaces. The dynamical behavior of macromolecules along interfaces and near walls is of biological interest and potentially may be studied by light scattering and fluorescence spectroscopy. In addition this problem is of theoretical interest because of the present day concern with two-dimensional transport phenomena and the difficulties encountered in the kinetic theory for the transport coefficients. We consider two polymer models, namely, rigid rods oriented perpendicularly to the interface, and diffuse spheres. In a fol-
lowing article we shall investigate the effect of solid walls on the translational diffusion of rigid rod molecules. We use an approximate expression for the diffusion tensor in terms of the hydrodynamic interaction tensor and the polymer segment distribution, which is a generalization of an expression derived by Kirkwood3 for diffusion in bulk fluids. The derivation for limited geometry and a discussion of the approximations involved is given in a separate article. In section I1 we consider a planar interface between two immiscible fluids and derive the corresponding fundamental solution of the linear Navier-Stokes equations for steady flow. We assume that the surface tension of the interface is so large that it remains planar. In section I11 we evaluate the translational diffusion coefficient for a rigid rod molecule oriented perpendicularly to the interface. In section IV we consider a spherical polymer and calculate its diffusion coefficient for motion along the interface. Finally, in section V we show that our assumption of large surface tension is an adequate approximation for the situa.cions of interest. 11. Hydrodynamic Interaction Tensor
We consider a polymer immersed in a fluid described by the creeping motion equations, Le., the Navier-Stokes
